CN1046555C - Steel material containing fine graphite particles uniformly dispersed therein and having excellent cold workability, machinability and hardenability and method of manufacturing the same - Google Patents
Steel material containing fine graphite particles uniformly dispersed therein and having excellent cold workability, machinability and hardenability and method of manufacturing the same Download PDFInfo
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- CN1046555C CN1046555C CN95192203A CN95192203A CN1046555C CN 1046555 C CN1046555 C CN 1046555C CN 95192203 A CN95192203 A CN 95192203A CN 95192203 A CN95192203 A CN 95192203A CN 1046555 C CN1046555 C CN 1046555C
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- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 90
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 78
- 239000010959 steel Substances 0.000 title claims abstract description 78
- 229910002804 graphite Inorganic materials 0.000 title claims abstract description 77
- 239000010439 graphite Substances 0.000 title claims abstract description 77
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 239000002245 particle Substances 0.000 title abstract description 11
- 239000000463 material Substances 0.000 title abstract description 4
- 238000001816 cooling Methods 0.000 claims abstract description 34
- 239000006185 dispersion Substances 0.000 claims abstract description 18
- 239000008187 granular material Substances 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 13
- 229910000754 Wrought iron Inorganic materials 0.000 claims description 10
- 238000012545 processing Methods 0.000 claims description 9
- 238000005087 graphitization Methods 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000013078 crystal Substances 0.000 description 15
- 229910000734 martensite Inorganic materials 0.000 description 15
- 238000010791 quenching Methods 0.000 description 15
- 229910000859 α-Fe Inorganic materials 0.000 description 15
- 238000005520 cutting process Methods 0.000 description 13
- 238000012360 testing method Methods 0.000 description 11
- 238000000137 annealing Methods 0.000 description 9
- 238000010273 cold forging Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 9
- 230000000171 quenching effect Effects 0.000 description 9
- 239000000126 substance Substances 0.000 description 9
- 230000009466 transformation Effects 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 8
- 239000004615 ingredient Substances 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- 230000006835 compression Effects 0.000 description 7
- 238000007906 compression Methods 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 229910001567 cementite Inorganic materials 0.000 description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 239000005864 Sulphur Substances 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 229910052796 boron Inorganic materials 0.000 description 3
- 238000007429 general method Methods 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 229910000915 Free machining steel Inorganic materials 0.000 description 2
- 229910003178 Mo2C Inorganic materials 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 150000001721 carbon Chemical group 0.000 description 2
- 239000000498 cooling water Substances 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000005553 drilling Methods 0.000 description 2
- 238000010894 electron beam technology Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000002075 main ingredient Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 238000012797 qualification Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 description 1
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 1
- 229910039444 MoC Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 150000001875 compounds Chemical group 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 230000009897 systematic effect Effects 0.000 description 1
- 230000003245 working effect Effects 0.000 description 1
Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/006—Graphite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D5/00—Heat treatments of cast-iron
- C21D5/04—Heat treatments of cast-iron of white cast-iron
- C21D5/06—Malleabilising
- C21D5/14—Graphitising
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16H—GEARING
- F16H61/00—Control functions within control units of change-speed- or reversing-gearings for conveying rotary motion ; Control of exclusively fluid gearing, friction gearing, gearings with endless flexible members or other particular types of gearing
- F16H61/14—Control of torque converter lock-up clutches
- F16H61/143—Control of torque converter lock-up clutches using electric control means
- F16H2061/145—Control of torque converter lock-up clutches using electric control means for controlling slip, e.g. approaching target slip value
Abstract
A fine graphite uniform dispersion steel material excellent in cold workability, cuttability and hardenability, which has graphite finely and uniformly dispersed therein, and a production method for producing the same. The steel contains at least 0.30 to 1.0% of C, 0.4 to 1.3% of Si, 0.3 to 1.0% of Mn, 0.0003 to 0.006% of B, 0.002 to 0.010% of N and 0.05 to 0.20% of Mo as the basic components and contains graphite having a mean particle diameter of not more than 4.0 mu m and a number of particles per unit and of at least 3,000 per mm2. The production method includes at least the steps of cooling the steel having these components at a cooling start temperature of not less than an Arl point, a cooling end temperature of not more than an Ms point and a mean cooling rate of 5 DEG to 100 DEG C./s.
Description
The present invention relates to cold working (forging, cutting etc.) after quench and the auto parts and the industrial machine element of temper, more particularly relate to the steel and the production method thereof of fine graphite even dispersion.
The Spheroidizing Annealing technology of cementite has been used to improve the cold forging of engineering steel, for example is used to improve the cold forging of AiSi1055 class steel, and easily cuts element such as sulphur, lead etc., then has been used to improve machinability.Yet cold forging and machinability, and hardening capacity and machinability be conflicting performance, all satisfy them simultaneously, is contradiction technically.
As a technology that solves these contradictions, have one piece of technical article relevant with the graphite dispersion steel delivered (Journal of the Japan Institute of Metals, Vol.30, No.3 (1966), p.279).This technology adds pearlite transformation with ferrite and becomes ferrite to add the tissue of graphite by the chemical ingredients and the annealing conditions of control steel under solid phase.This chemical ingredients for example is: C0.24%, and Si1.18%, Mn0.24%, Ni2.03%, graphitizing annealing is handled 650 ℃ of Heating temperatures, and carry out under the about 28 hours condition heat-up time.Cold forging about this system steel grade, technical article " Journal of the Japan Institute of Metals ", Vol.53 (1989), P.206 report is said, when adding pearlitic structure, the ferrite of medium carbon steel is transformed into ferrite when adding the duplex structure of graphite, its hardness drops to Hv according to Vickers' hardness by Hv160 and is about 110, and its cold forging becomes and is higher than the sulphur free-cutting steel.At " Journal of Japan Institute ofMetals ", Vol.52 (1988), p.1285 in, also machinability is narrated.This piece paper report says that when the greying ratio became big, the feed component of the main component of anti-cutting and anti-cutting is actual to drop to half, and shearing stress becomes big along with the angle of shear and frictional coefficient diminishes and reduce, and the radius of smear metal circle diminishes, and makes the processibility improvement.
But existing graphite dispersion steel does not use in industry, and this is because as described in the public clear No.53-46774 of spy, in the mixture of the graphite granule that the described technology according to the document obtains, has the graphite granule that diameter surpasses 30 μ m.In other words, when big and these particles were non-even dispersion when the graphite granule size, when quench hardening, the dissolving of graphite in austenite was inadequate, and it is longer that diffusion length becomes, and carbon atom generation segregation.Generation quench hardening as a result is insufficient, and quench hardening is inhomogeneous, or the like.Particularly under induction hardened situation, in short-term, the tissue of steel may become martensite and add ferritic mixed structure as several seconds the duration of heat.When the graphite granule chap, cold forging can ftracture, and ultimate strain diminishes, and the surfaceness of cutting after finishing becomes big.
In a word, obtain concrete application in order to make the aquadag steel, basic condition is refinement graphite and makes its even dispersion.Thereby the situation of the technology of following narration control aquadag steel graphite granule diameter and disperse thereof.At first, the spy opens flat 2-111842 and has narrated the precipitation nuclear that BN can be used as graphite, and it to be not more than 30ppm for the restriction oxygen level be effective.BN is known in this technical field effectively to graphite refinement precipitation.But,, thereby utilize this BN also to segregate in the ferrite crystal grain interface as the graphite of precipitation nuclear because BN is segregated in austenitic crystal boundary.In other words, can't reach the even dispersion of graphite by chemical ingredients.
Then narrate the technology status of the production method of even dispersion fine graphite.By introduce aquadag nuclear in following two pieces of documents to promote graphited idea that narration is arranged: " Joural of theJapan Institute of Metals ", Vol.30 (1996), P.279 and No.7, Vol.43 (1979), p.460.It is effective as aquadag nuclear that these papers have been narrated the supersaturation of carbon in the ferrite, martensitic transformation strain and processing strain.
Below explain the prior art of using above-mentioned idea.The spy opens clear 49-67817 and has disclosed a kind of method, and this method is utilized the hypersaturated state (martensitic stucture) and the martensitic transformation strain of carbon.This piece document provides a kind of production method, and this method comprises and will contain C (total amount) 0.45-1.5%, graphite 0.45-1.5%, Si0.5-2.5%, Mn0.1-2.0%, P0.02-0.15%, S0.001-0.015%, N0.008-0.02%, Ni0.1-2.0%, at least a 0.015-0.5% of Al and Ti, and the steel hot rolling of Ca0.0005-0.030%, it is quenched at 750-950 ℃ of reheat, causing Martensite Transformation, and then this steel is annealed in 600-750 ℃ of reheat.Because this production method do not give the processing strain, so graphited annealing time is elongated, and because the heating steps after the hot rolling needs twice, institute so that production cost uprise.
The spy opens clear 63-9580 and has narrated a kind of utilization processing strained method.The method of this piece document illustration comprises: will contain C0.015-0.140%, Mn is not more than 0.3%, solid solution Al0.02-0.30%, and N is not more than 0.006%, and P is not more than 0.01%, and S is not more than 0.010%, wherein satisfied P * S≤10 * 10 that concern of P (%) * S (%)
-6, below three kinds of elements at least a: Si0.03-2.50%, Ni0.1-4.0% and Cu0.03-1.00%, all the other are the steel hot rolling of Fe and impurity, this steel are carried out cold rollingly at least with compression ratio 30% again, to cause the processing strain, anneal then.But can not say so under the situation of bar steel and wire rod a kind of method of practicality of this production method is because its requires can carry out cold rolling step with compression ratio 30% after hot rolling.
As mentioned above, for obtaining the steel of the good fine graphite even dispersion of cold machinability, machinability and hardening capacity, existing chemical ingredients and production method also do not solve various problems.Thereby they also are not used with the scale of industry.
Purpose of the present invention is exactly for addressing the above problem, by improving chemical ingredients and working condition, the steel and the production method thereof of the good fine graphite even dispersion of a kind of cold machinability, machinability and hardening capacity are provided, with the average particulate diameter (mean sizes in the room, back of quenching) that reduces graphite, and make graphite, but also in the disperse equably of the inside of ferrite crystal grain not only at crystal boundary.
Main points of the present invention are following each point.
(1) steel of the fine graphite even dispersion that a kind of cold machinability, machinability and hardening capacity are good, as main ingredient by weight the percentage ratio meter contain: C0.30-1.0%, Si0.4-1.3%, Mn0.3-1.0%, P≤0.03%, S0.010-0.055%, Al0.01-0.10%, B0.0003-0.006%, N0.002-0.010% and Mo0.05-0.20%, all the other are Fe and unavoidable impurities, and contain the graphite 0.3-1.0% that average particulate diameter is not more than 4.0 μ m, and its number of particles is at least 3000/mm
2
(2) a kind of cold machinability, machinability and hardening capacity of producing is good, the fine graphite even dispersion and contain graphite 0.3-1.0% and its number of particles that average particulate diameter is not more than 4.0 μ m and be at least 3000PCS/mm
2The method of steel, said method comprises: will as main ingredient by weight the percentage ratio meter contain C0.30-1.0%, Si0.4-1.3%, Mn0.3-1.0%, P≤0.03%, S0.010-0.055, Al0.01-0.10%, B0.0003-0.006, N0.002-0.010% and Mo0.05-0.20%, all the other are the steel of Fe and unavoidable impurities, after being rolled into rod iron, the water cooling equipment that use is configured in after the hot rolling line is cooled off immediately, and cooling beginning temperature is not less than Ar
1Point, the cooling end temp is not higher than the Ms point, and average rate of cooling 5-100 ℃/S again with its naturally cooling, carries out graphitization processing then under Heating temperature 600-720 ℃.
Fig. 1 (a), 1 (b) and 1 (c) be respectively according to prior art AiSi1055, according to the graphitized steel of prior art with according to the metallograph of the metal structure of steel of the present invention.
Fig. 2 is the SEM photo according to graphitized steel metal structure of the present invention.
The present inventor has carried out a series of research, finds first: when adding Mo, graphite granule digital display work increases, and the particle size of graphite diminishes, the position of also finding precipitation occurs in crystal grain boundary again both in the inside of ferrite crystal grain, and equably disperse of graphite.
This is because Mo according to estimates2The crystal structure of C is the hexagonal crystal system identical with BN, and Mo2C is as the precipitation nuclear of the graphite with same hexagonal crystal system. The chances are for the reason of graphite even dispersion because Mo2C is regardless of being even dispersion of crystal grain boundary and crystal grain the inside.
But, as Unexamined Patent 2-111842 narrate, think that in the past Mo is the element of solid solution in cementite, its postpones the decomposition of cementite, and finally with the obstruction of the same manner of Cr role graphitization. Opposite with this common concept, the inventor has given special attention to the following fact, i.e. Mo hardly solid solution in cementite, and find first: molybdenum carbide can be used as the precipitation nuclear of graphite, and has the effect of refinement and even dispersion graphite granule.
Then narrate production method.
The inventor has been found that by being configured in hot rolling line water cooling equipment afterwards, cool off rod iron immediately after hot rolling.This cooling beginning temperature is not less than Ar
1Point, cooling termination temperature are not higher than Ms, and average rate of cooling 5-100 ℃, make the rod iron naturally cooling again, under 600-720 ℃ Heating temperature, carry out graphitization processing then, just can refinement graphite.It is believed that because except the martensitic transformation strain, in martensite, added because of the rolling strain of cooling reservation fast after the hot rolling, thus the increase of the strain total amount in the martensite, thereby the nucleation site of graphite increases.
Explain that below the present invention limits the reason of content.About first invention, it is for the intensity after guaranteeing to anneal that the lower value of C is decided to be 0.30%, and guarantees to obtaining the satisfied needed quantity of graphite of cutting ability.With being defined as 1.0% on it is in order to prevent its hardening break when the cold working postheat treatment.
Si is a kind of indispensable element, and this is because its binding ability with carbon atom in steel is little, and it still promotes graphited useful element.Si must add, so that the graphite of precipitation q.s, and by the high greying ratio of quenching+anneal acquisition.Thereby its lower value must be at least 0.4%.But when content surpasses 1.3%,, become higher, make cold-workability descend in the increase of Si amount and the hardness of solid solution in ferritic phase though the greying ratio uprises.Since through greying hardness reduce the effect be cancelled, so will on be defined as 1.3%.
The Mn that added amount be in steel with the form of MnS the fixing and needed amount of disperse sulphur and in matrix, cause its solid solution and proof strength aequum sum thus, its lower value is 0.3%.When the Mn quantitative change was big, greying was subjected to significant obstruction, thereby its higher limit is decided to be 1.0%.
P exists with the compound form of sedimentary phosphorus in the crystal grain boundary of structure of steel with the form through the P of solid solution in ferrite.Although P has improved machinability, it has significantly reduced hot workability.Thereby will be defined as 0.03% on it.
S combines with Mn and exists with MnS inclusion form.When the amount of MnS inclusion in the steel increased, the touch opportunity between instrument and the MnS inclusion increased, and the MnS inclusion stands viscous deformation and forms film on tool-face.Touch opportunity between ferrite and the instrument reduces as a result, and bonding is restricted, and can improve the performance of final cutting surface.Be the restriction bonding, the lower value of S needs 0.01% at least.Because S reduces cold forging, so its higher limit is decided to be 0.055%.
Al is with form deoxidation in steel of oxide type inclusion.For adjusting the size of crystal grain, must add at least 0.01% Al.Because at Al content is that 0.10% o'clock deoxidation effect becomes saturated, so its higher limit is decided to be 0.10%.
B and N form BN and reduce the time of graphitizing annealing.In order fully to obtain the effect of this minimizing, must add 0.0003% B at least.But when B content surpassed 0.006%, the effect of this minimizing became saturated.Thereby will be defined as 0.006% on it.The content range of N is 0.002-0.010%, so that the B of 0.0003%-0.006% is transformed into BN.
Mo plays as the effect that forms aquadag nuclear.In order to fix on 3000/mm by number with graphite granule
2To reduce average particle size particle size (being not more than 4 μ m), the number that must guarantee precipitation nuclear is greater than certain number.
Thereby must add 0.05% Mo at least.The uniform disperse of result had not only been finished in the ferrite crystal grain interface but also in particulate inside.When Mo content surpassed 0.20%, above-mentioned effect became saturated, and the hardness of ferrite matrix rises.Thereby its higher limit is decided to be 0.20%.
Angle by hardening capacity is set out, and the upper limit of the average particle size particle size of graphite is necessary for 4 μ m.When it surpassed 4 μ m, quenching structure became ferrite and martensitic mixed structure, and the heterogeneity of hardness becomes remarkable.When the number of graphite granule less than 3000/mm
2The time, the distance between the graphite granule increases, and the diffusion length of carbon becomes excessive.Thereby quenching structure becomes martensite and ferritic incomplete quenching structure.Thereby lower value is necessary for 3000/mm
2Because be with the full dose of C in steel greying basically, so the lower value of graphite must be consistent with the lower value of C content, be 0.30%, and its higher limit must be consistent with the higher limit of C content, be 1.0%.
Below limit the reason of chemical ingredients and working condition in narration the 2nd invention of the present invention.
To C, Si, Mn, P, S, Al, B, the qualification in the qualification of N and Mo and the 1st invention is in full accord.About working condition, to force the reason of cooling steel be the strain that causes because of hot rolling for reservation in the quenched martensite tissue with being configured in water cooling plant after the hot rolling line immediately after hot rolling finish to gauge.According to the method, the heat energy that is in the steel of red heat state after the hot rolling can be used to quench, and need not reheat.The result has reduced heat treated expense.
In order to produce martensitic transformation strain and rolling strain simultaneously, begin temperature by the cooling of measuring on the steel surface and must be not less than Ar to increase the number of aquadag nuclear
1The point.For fully obtaining the martensitic transformation tissue and making that formation graphite is easy, cool off finishing temperature and must not be higher than the Ms point.The lower value of average rate of cooling is made as the reason of 5 ℃/S, is for obtaining the martensitic transformation tissue and processing strain to promote greying by keeping.Its higher limit is decided to be the reason of 100 ℃/S, even be because quench to surpass this speed, can not increase the quantity of martensitic transformation.Annealed higher limit and lower value are decided to be the reason of 600 ℃ and 720 ℃ respectively, are because graphitization time becomes the shortest in this temperature range.
Followingly more specifically narrate effect of the present invention with reference to embodiment.
Embodiment
It is the chemical ingredients of the present invention and the working condition of example that table 1 has been listed with rod iron and wire rod.The rod iron and the wire rod diameter that are used for this test are 10-30mm.By being configured in hot rolling line cooling apparatus afterwards, with per unit area 0.3-0.5t/m
2The even shower cooling water of speed to whole rod iron surface, to cool off every rod iron.Cooling apparatus is made of the pipe of length 20m and the many spray orifices that are used for shower cooling water around it, when the center line movement of rod iron at this pipe it is cooled off.Every wire rod is then by making its be cooled through the water-cooled jar that is configured in behind the hot rolling line.Average rate of cooling is begun the difference of temperature and cooling finishing temperature divided by determining cooling time by cooling.With the test specimen naturally cooling, the annealing furnace by off-line carries out graphitization processing more then.
Table 1
| C (％) | Si (％) | Mn (％) | P (％) | S (％) | Al (％) | Mo (％) | B (％) | N (％) | Direct quenching after the hot rolling | The graphitizing annealing temperature (℃) | The graphitizing annealing time (hr) | ||||
| Cooling beginning temperature (℃) | The cooling finishing temperature (℃) | Average rate of cooling ℃/s | |||||||||||||
| Steel of the present invention | A | 0.55 | 1.15 | 0.55 | 0.011 | 0.023 | 0.016 | 0.10 | 0.003 | 0.004 | 860 | 180 | 86 | 680 | 10 |
| B | 0.60 | 1.20 | 0.45 | 0.013 | 0.021 | 0.022 | 0.15 | 0.002 | 0.004 | 820 | 100 | 81 | 680 | 10 | |
| C | 0.48 | 1.01 | 0.51 | 0.015 | 0.016 | 0.023 | 0.07 | 0.002 | 0.005 | 810 | 180 | 25 | 660 | 10 | |
| D | 0.52 | 0.70 | 0.79 | 0.011 | 0.035 | 0.025 | 0.20 | 0.003 | 0.003 | 870 | 180 | 10 | 690 | 10 | |
| E | 0.40 | 1.25 | 0.55 | 0.012 | 0.021 | 0.024 | 0.14 | 0.002 | 0.003 | 740 | 210 | 68 | 670 | 10 | |
| General steel | F | 0.50 | 0.52 | 1.02 | 0.010 | 0.010 | 0.022 | - | 0.003 | 0.004 | - | - | - | 630 | 20 |
| C | 0.55 | 0.22 | 0.35 | 0.012 | 0.012 | 0.023 | - | 0.003 | 0.005 | - | - | - | 650 | 25 | |
| H | 0.52 | 0.51 | 0.72 | 0.013 | 0.015 | 0.023 | - | 0.002 | 0.005 | - | - | - | 610 | 18 | |
| I | 0.54 | 0.20 | 1.20 | 0.015 | 0.011 | 0.022 | - | 0.002 | 0.004 | - | - | - | 520 | 16 | |
| J | 0.55 | 0.20 | 1.01 | 0.013 | 0.010 | 0.021 | - | 0.002 | 0.003 | - | - | - | 810 | 12 | |
Table 2 shows the evaluation result and its performance (cold forging, the rangeability of the final surfaceness and the back hardness of quenching) of graphite dispersivity (graphite granule size, ultimate range between graphite and quantity of graphite).The measuring method of graphite granule size is as follows.
Electron beam is radiated on the graphite granule,, on the SEM screen, forms image, operational analysis systematic survey and the analysing particulates diameter of graphite by the intensity digitizing of electron beam that will reflection.The area of a visual field is 100 μ m * 100 μ m, and the visual field number of observing is 25.Total survey area is 0.25 μ m.On 200 times opticmicroscope, measure the ultimate range between graphite.On photo, show the circle that only comprises the part that does not have graphite, and with the maximum value of its diameter as the ultimate range between graphite.The steel that ultimate range between graphite granule of the present invention and graphite makes less than usual way.
Table 2
Quantity of graphite is calculated as follows: (in the steel in content of graphite/steel carbon content) * 100 (%)
| The average crystal grain diameter μ m of graphite | The number cps/mm of graphite 2 | Quantity of graphite (%) | Ultimate range μ m between graphite | Manufacturing limit (%) | Final surfaceness Rz (μ m) | Quenching hardness scope Hv | ||
| Steel of the present invention | A | 2.5 | 5300 | 0.55 | 58 | 83 | 12 | 725-750 |
| B | 2.3 | 4500 | 0.60 | 55 | 84 | 11 | 735-752 | |
| C | 3.8 | 3800 | 0.48 | 76 | 83 | 13 | 715-745 | |
| D | 1.2 | 5200 | 0.52 | 52 | 82 | 10 | 716-742 | |
| E | 2.2 | 3500 | 0.40 | 60 | 82 | 13 | 718-726 | |
| General steel | F | 19.9 | 200 | 0.45 | 240 | 71 | 28 | 420-650 |
| G | 12.3 | 420 | 0.47 | 280 | 70 | 28 | 480-645 | |
| H | 8.7 | 1250 | 0.50 | 126 | 73 | 19 | 520-640 | |
| I | 9.2 | 960 | 0.48 | 170 | 71 | 22 | 389-635 | |
| J | 20.5 | 250 | 0.49 | 252 | 69 | 29 | 402-638 | |
Carbon content in the steel and quantity of graphite are determined through chemical analysis.Although annealing time is as short as about 10 hours, the greying ratio of rod iron of the present invention presents 100% splendid value.And press general method, the greying ratio is low to reach about 50%.
Steel of the present invention, the steel that makes by general method and be shown in Fig. 1 by the graphitized steel that general method makes with comparing.Fig. 1 (a), 1 (b) and 1 (c) illustrate conventional AiSi1055 respectively, conventional graphitized steel and steel of the present invention.In addition, Fig. 2 is a width of cloth SEM photo, and the graphite that amplifies in the steel of the present invention is shown.As can be seen, the graphite in the steel of the present invention has the form that spherical graphite is arranged that is similar at microscopically.In the general graphitized steel that is shown in Fig. 1 (b), graphite is thick and segregation takes place, but in steel of the present invention, as appreciable by corresponding photo, graphite granule is disperse equably.
Estimate cold forging through comparison test.Be of a size of each test specimen of φ 14mm * 21mm, use, with the 200mm/ speed compression of second at the oil pressure test machine that has on the instrument of concentric groove.In the moment that the test specimen surface occurs, measure the height of test specimen, and compression ratio (e) is determined at crackle by following equation:
e={1-(H/Ho)}×100％
In the formula, H: the height of test back test specimen,
Ho: the height of test specimen before the test.
Though the manufacturing limit of general steel is about 73% by compression ratio, the compression ratio of steel of the present invention is up to 83%.Although the difference by compression ratio is 10%, when this difference was converted to the strain that blank accepts, logarithmic strain was respectively 1.3 and 1.8.Thereby 40% difference arranged.
Final surface smoothness is carried out surfacing cut through using the superhard alloy cutter that is coated with TiN, and uses the probe-type surfagauge to estimate.Machining condition is: V=250m/min, t=0.2mm/rev, and d=2.0mm.The final surface smoothness of steel of the present invention is extremely good.
Hardening capacity is estimated by the following method, and the pole of diameter 25mm is quenched (1000 ℃ * 3s → water-cooled) through the induction quenching mode under the aquadag state, measures the changes in hardness amplitude in pole cross section then.Can find out the hardening capacity of the hardening capacity of steel of the present invention far above general steel.
About machinability, under situation, to compare with the graphitized steel of routine with final surface smoothness, steel of the present invention is greatly improved, and superior more than original lead and easy-cutting steel.Table 3 shows, and compare the work-ing life of drill bit during with the existing lead and easy-cutting steel of boring cutting, and drilling life of bit wanted much good when steel of the present invention was holed cutting.This is to have ferrite and pearlitic structure because be used for the conventional free-cutting steel of physical construction, and graphitized steel has the ferrite graphite structure, and in the latter case, the hardness of material self is significantly lower.The chemical ingredients of existing lead and easy-cutting steel is: C0.41%, and Si0.22%, Mn1.58%, S0.057%, Pb0.20% and Ca0.0011%, drill bit material are a kind of rapid steel, have following shape: diameter 10mm, length 130mm, toe angle is 118 °.Advancing the drilling speed degree is 0.33mm/rev, and after the hole that gets out a large amount of dark 30mm, the time that drill bit is damaged fully is as the life-span.When total hole depth is 1000mm, then use the circumferential speed (V of the drill bit that reaches bit life
L1000) as the judgement reference of affirmation and negation machinability.The V of steel of the present invention
L1000Value is 146m/min.Be understandable that this value substantially exceeds the 66m/min of lead and easy-cutting steel.
Table 3
| V L1000 m/min | ||
| Steel of the present invention | A B | 146 148 |
| Existing lead and easy-cutting steel | 66 | |
As can know by the foregoing description understanding, the present invention can provide have good cold-workability, good machinability and steel good hardening capacity, the fine graphite even dispersion, thereby the present invention has extremely significant industrial effect.
Claims (2)
1. the steel of the fine graphite even dispersion that cold-workability, machinability and hardening capacity are good is characterized in that, the consisting of of this steel: percentage ratio by weight,
C:0.30-1.0％
Si:0.4-1.3％
Mn:0.3-1.0％
P:≤0.03％
S:0.010-0.055％
Al:0.01-0.10％
B:0.0003-0.006％
N:0.002-0.010％
Mo:0.05-0.20％
All the other are made of Fe and unavoidable impurities, and contain the graphite of 0.3-1.0%, and its average particulate diameter is not more than 4.0 μ m and granule number is at least 3000/mm
2
2. the method for the homodisperse steel of fine graphite that production cold-workability, machinability and hardening capacity are good, this steel contains the graphite of 0.3-1.0%, and its average particulate diameter is not more than 4.0 μ m, and granule number is at least 3000/mm
2, it is characterized in that said method comprises, will consist of: percentage ratio meter by weight,
C:0.30-1.0％
Si:0.4-1.3％
Mn:0.3-1.0％
P:≤0.03％
S:0.010-0.055％
Al:0.01-0.10％
B:0.0003-0.006％
N:0.002-0.010％
Mo:0.05-0.20％
All the other are the steel of Fe and unavoidable impurities, and after being rolled into rod iron, the water cooling equipment that use is configured in after the hot rolling line is cooled off immediately, and cooling beginning temperature is not less than Ar
1Point, the cooling end temp is not higher than the Ms point, average rate of cooling 5-100 ℃/S;
Again with said steel naturally cooling; Then
Under Heating temperature 600-720 ℃, carry out graphitization processing.
Applications Claiming Priority (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02693994A JP3150523B2 (en) | 1994-02-24 | 1994-02-24 | Method for producing hypoeutectoid graphite deposited steel wire |
| JP26939/94 | 1994-02-24 | ||
| JP06220804A JP3093577B2 (en) | 1994-08-24 | 1994-08-24 | Fine graphite uniformly dispersed steel bar with excellent toughness and method for producing the same |
| JP06220803A JP3093576B2 (en) | 1994-08-24 | 1994-08-24 | Fine graphite uniformly dispersed steel wire with excellent toughness and method for producing the same |
| JP220803/94 | 1994-08-24 | ||
| JP220804/94 | 1994-08-24 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1144543A CN1144543A (en) | 1997-03-05 |
| CN1046555C true CN1046555C (en) | 1999-11-17 |
Family
ID=27285597
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN95192203A Expired - Lifetime CN1046555C (en) | 1994-02-24 | 1995-02-24 | Steel material containing fine graphite particles uniformly dispersed therein and having excellent cold workability, machinability and hardenability and method of manufacturing the same |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US5830285A (en) |
| EP (1) | EP0751232B1 (en) |
| KR (1) | KR100210867B1 (en) |
| CN (1) | CN1046555C (en) |
| CA (1) | CA2183441C (en) |
| DE (1) | DE69514340T2 (en) |
| WO (1) | WO1995023241A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| SE9800860L (en) * | 1998-03-16 | 1999-05-25 | Ovako Steel Ab | Ways for soft annealing of high carbon steel |
| JP3702618B2 (en) * | 1997-11-04 | 2005-10-05 | 日本精工株式会社 | Toroidal type continuously variable transmission |
| JP4119516B2 (en) * | 1998-03-04 | 2008-07-16 | 新日本製鐵株式会社 | Steel for cold forging |
| RU2135617C1 (en) | 1998-04-23 | 1999-08-27 | Дорофеев Генрих Алексеевич | Alloy with free and fixed carbon and method of its production |
| US6390924B1 (en) * | 1999-01-12 | 2002-05-21 | Ntn Corporation | Power transmission shaft and constant velocity joint |
| US8283296B2 (en) * | 2006-10-11 | 2012-10-09 | Henkel Ag & Co., Kgaa | Lubricant for hot forging applications |
| RU2494152C2 (en) * | 2011-10-12 | 2013-09-27 | Открытое акционерное общество "КАМАЗ" | Method of iron carbonisation by means of nano-structured carboniser |
| RU2600460C2 (en) * | 2012-06-28 | 2016-10-20 | ДжФЕ СТИЛ КОРПОРЕЙШН | Tube from high-carbon steel with excellent processability in cold state, processability and hardenability and its manufacturing method |
| JP2016014169A (en) * | 2014-07-01 | 2016-01-28 | 株式会社神戸製鋼所 | Wire rod for steel wire and steel wire |
| KR101657790B1 (en) * | 2014-12-09 | 2016-09-20 | 주식회사 포스코 | Steel material for graphitization and graphite steel with excellent machinability and cold forging characteristic |
| KR102010052B1 (en) * | 2017-10-19 | 2019-08-12 | 주식회사 포스코 | Medium carbon free cutting steel having excellent hot workability and method for manufacturing the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPS4957817A (en) * | 1972-10-02 | 1974-06-05 | ||
| JPS5346774B2 (en) * | 1973-02-07 | 1978-12-16 | ||
| JPH02111842A (en) * | 1988-06-30 | 1990-04-24 | Kawasaki Steel Corp | Hot rolling steel stock excellent in machinability and hardenability |
| JPH04124216A (en) * | 1990-09-12 | 1992-04-24 | Sumitomo Metal Ind Ltd | Production of high carbon steel sheet having superior formability |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5315451B2 (en) * | 1972-11-06 | 1978-05-25 | ||
| JPS5346774A (en) * | 1976-10-08 | 1978-04-26 | Seiko Epson Corp | Electronic wristwatch |
| US5476556A (en) * | 1993-08-02 | 1995-12-19 | Kawasaki Steel Corporation | Method of manufacturing steel for machine structural use exhibiting excellent free cutting characteristic, cold forging characteristic and post-hardening/tempering fatigue resistance |
| JP2907700B2 (en) * | 1993-11-12 | 1999-06-21 | 新日本製鐵株式会社 | Hypoeutectoid graphite precipitated steel with excellent quenching performance and fatigue strength |
| JPH07188851A (en) * | 1993-12-28 | 1995-07-25 | Kawasaki Steel Corp | Graphite free-cutting steel excellent in machinability |
| JPH07188850A (en) * | 1993-12-28 | 1995-07-25 | Kawasaki Steel Corp | Graphite free-cutting steel excellent in machinability |
-
1995
- 1995-02-24 DE DE69514340T patent/DE69514340T2/en not_active Expired - Lifetime
- 1995-02-24 EP EP95909974A patent/EP0751232B1/en not_active Expired - Lifetime
- 1995-02-24 WO PCT/JP1995/000276 patent/WO1995023241A1/en active IP Right Grant
- 1995-02-24 CA CA002183441A patent/CA2183441C/en not_active Expired - Lifetime
- 1995-02-24 KR KR1019960704638A patent/KR100210867B1/en not_active IP Right Cessation
- 1995-02-24 US US08/700,355 patent/US5830285A/en not_active Expired - Lifetime
- 1995-02-24 CN CN95192203A patent/CN1046555C/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4957817A (en) * | 1972-10-02 | 1974-06-05 | ||
| JPS5346774B2 (en) * | 1973-02-07 | 1978-12-16 | ||
| JPH02111842A (en) * | 1988-06-30 | 1990-04-24 | Kawasaki Steel Corp | Hot rolling steel stock excellent in machinability and hardenability |
| JPH04124216A (en) * | 1990-09-12 | 1992-04-24 | Sumitomo Metal Ind Ltd | Production of high carbon steel sheet having superior formability |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1144543A (en) | 1997-03-05 |
| DE69514340T2 (en) | 2000-08-24 |
| EP0751232A1 (en) | 1997-01-02 |
| EP0751232B1 (en) | 2000-01-05 |
| DE69514340D1 (en) | 2000-02-10 |
| CA2183441C (en) | 2000-05-23 |
| WO1995023241A1 (en) | 1995-08-31 |
| EP0751232A4 (en) | 1997-05-21 |
| CA2183441A1 (en) | 1995-08-31 |
| US5830285A (en) | 1998-11-03 |
| KR100210867B1 (en) | 1999-07-15 |
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